EP3645756A1 - Acier à trempe martensitique et son utilisation, en particulier pour fabriquer une vis - Google Patents

Acier à trempe martensitique et son utilisation, en particulier pour fabriquer une vis

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Publication number
EP3645756A1
EP3645756A1 EP18735215.8A EP18735215A EP3645756A1 EP 3645756 A1 EP3645756 A1 EP 3645756A1 EP 18735215 A EP18735215 A EP 18735215A EP 3645756 A1 EP3645756 A1 EP 3645756A1
Authority
EP
European Patent Office
Prior art keywords
screw
blank
steel
weight
carbon
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP18735215.8A
Other languages
German (de)
English (en)
Other versions
EP3645756B1 (fr
Inventor
Roland Schneider
Michael Bischof
Alexander Tomandl
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hilti AG
Original Assignee
Hilti AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Hilti AG filed Critical Hilti AG
Publication of EP3645756A1 publication Critical patent/EP3645756A1/fr
Application granted granted Critical
Publication of EP3645756B1 publication Critical patent/EP3645756B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/04—Hardening by cooling below 0 degrees Celsius
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0093—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for screws; for bolts
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/28—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases more than one element being applied in one step
    • C23C8/30—Carbo-nitriding
    • C23C8/32—Carbo-nitriding of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • Martensitic hardenable steel and its use, in particular for producing a screw
  • the invention relates to a method for producing a shaped body, in particular a hardened shaped body, from a blank, a steel, its use for producing a screw and a screw.
  • bimetallic screws which are characterized in that on the screw body, ie on the head and the shaft, made of austenitic stainless A2 or A4 steel (comparable 1.4301 or 1.4401) a bolt made of hardenable carbon steel is welded. This bolt is hardened after welding and forming by means of a local heat treatment. Even such screws can be relatively expensive to manufacture.
  • DE4033706 A1 describes a heat treatment method for increasing the corrosion resistance of a hardened surface layer of near-net-shaped components made of martensitic stainless steels with less than 0.4% by weight of carbon by diffusion of 0.2 to 0.8% by weight of nitrogen into the surface layer.
  • an application in screws is not taught by DE4033706 A1 and in particular is the DE4033706 A1 is not based on a coordination of the chemical composition of the steel and the heat treatment parameters for use in screws.
  • DE19626833A1 describes a method for producing a highly corrosion-resistant martensitic surface layer over a ferritic-martensitic core in components made of stainless steel.
  • the chemical composition of the steel is limited such that a ferritic-martensitic structure is present and after case hardening at a temperature of 1050 ° C - 1 150 ° C with nitrogen, the ferrite content in the core between 40 and 90 vol .-% and the core hardness less than 300 HV30.
  • An application of the method for screws is not taught again.
  • DE102013108018 A1 describes a screw made of a stainless steel, for example 1 .41 13, wherein the steel is substantially free of nickel, wherein an edge layer due to a nitrile heat treatment at 1000-1200 ° C has a content of dissolved nitrogen compared to the rest of the structure , and wherein the screw in the boundary layer has a martensitic structure and otherwise a ferritic structure.
  • W014040995 A1 describes a method for producing a self-tapping concrete screw, in which a blank of a martensitic hardenable steel, in particular with a carbon content less than 0.07%, is cured at a temperature greater than 900 ° C in a nitrogen-containing gas atmosphere.
  • TW201418549 A describes a screw with a steel comprising 0.26 to 0.40% carbon, 12 to 14% chromium, 0 to 0.6% nickel and 0 to 1% manganese.
  • the object of the invention is to provide a method for producing a shaped body, in particular a helical shape, from a steel blank as well as a corresponding steel, with which at particularly low production costs and high product reliability, especially for screw applications, especially advantageous combination of surface hardness, core toughness and corrosion resistance, resistance to hydrogen and chloride induced embrittlement and workability, in particular formability, can be realized. It is another object of the invention to provide a use of such a steel and a screw comprising such a steel, with which the aforementioned advantages can be implemented.
  • a method according to the invention is used for producing a shaped body, preferably a helical shape, and uses a blank comprising a steel with a weight fraction of 0.07 to 0.14% by weight of carbon, 13 to 15% by weight of chromium, 1.3 to 1, 7 wt .-% molybdenum, 1, 5 to 2.0 wt .-% nickel and 1, 0 to 1, 5 wt .-% manganese.
  • the steel may have other admixtures customary in the steel, for example vanadium (in particular ⁇ 0.2% by weight), niobium (in particular ⁇ 0.2% by weight), titanium (in particular ⁇ 0.2% by weight) and / or silicon (in particular ⁇ 0.5% by weight).
  • the remainder is iron with unavoidable impurities, for example sulfur and / or phosphorus, in particular in each case ⁇ 0.02% by weight.
  • the steel may be referred to as a martensitic hardenable stainless steel
  • the steel has a weight fraction of from 0.08 to 0.12% by weight of carbon on.
  • the invention is based on the recognition that stainless martensitic steels can be promising candidates to meet the partially conflicting steel requirements that may arise when used in screws, especially in self-tapping screws.
  • the chemical composition of the steel in particular with regard to the alloy constituents carbon, chromium, molybdenum, nickel and manganese
  • the required for the adjustment of the property profile multi-stage heat treatment consisting of Hochtemperaturgasaufsticken, gas phase quenching, low-temperature cooling, tempering and optional local induction hardening are carefully matched.
  • Previous concepts according to the prior art are often based on a rather unfavorable for a screw combination of chemical Composition of the stainless martensitic steel and the heat treatment, so that often not all required for a screw properties could be sufficiently satisfied simultaneously.
  • the steel grade 1.4313 (X3CrNiMo13-4) is a representative of the soft-martensitic steel group. This type of stainless martensitic steels is often also suitable for use in screws often limited, because the steels often have only a relatively low surface hardness and often still too low corrosion resistance for screw application.
  • Stainless martensitic steels offer the option of setting the combination of high surface hardness and simultaneously lower core hardness (equivalent to good toughness and high resistance to chloride- or hydrogen-induced embrittlement) and good corrosion resistance by case-hardening with nitrogen instead of carbon.
  • Nitrogen which is dissolved in such a case hardening in the component increases the surface hardness, corrosion resistance and compressive residual stress of the surface layer. Due to the nitrogen dissolved in the surface layer of the component, this heat treatment method is also referred to as "solution nitriding".
  • the invention includes a steel whose chemical composition is based on a combination of the alloying constituents carbon (0.07-0.14 wt.%, Preferably 0.08 - 0.12 wt .-%), chromium (13 - 15 wt .-%), molybdenum (1, 3 - 1, 7 wt .-%), nickel (1, 5 - 2.0 wt .-%) and manganese (1, 0 to 1, 5 wt .-%, preferably 1, 2 wt .-%) is based.
  • a property profile could be realized, which is characterized by a good formability of the blank, a high surface hardness of 580 HV0.3 or higher, a maximum core hardness of 450 HV0.3 or less, a high resistance to general corrosion and pitting in the core ( by a PRE index of 17 or higher) and in the periphery (represented by a PRE index of 23 or higher), high core toughness (especially as a result of a combination of low carbon content and stable delta ferrite, thereby increasing coarse grain growth is suppressed in the heat treatment) and a high resistance to chloride- or hydrogen-induced embrittlement is characterized.
  • the steel may be advantageous in particular in the following respect:
  • the core hardness is 450 HV0.3 or less.
  • a relatively high PRE Index (Pitting Resistance Equivalent), preferably 17 or higher, can be achieved without, however, leaving the state domain of a martensitic or martensitic-ferritic microstructure.
  • the steel has a good processability to semifinished forms such as wire rod or drawn bare wire. Both rolled and bare wire have a good cold workability, preferably represented by a yield strength R p 0.2 ⁇ 650 N / mm 2 , which may be particularly advantageous for the production of screws in a cold forming process, preferably with a rolling process.
  • a predominantly austenitic structure (preferably between 70% - 95%) with a small Set proportion of delta ferrite in the extent of 5% - 30%, with this delta ferrite content of 5% - 30% can have a stabilizing effect on the structure at said temperatures and thereby counteract Kornvergroberung what can have an advantageous effect on the toughness properties.
  • the delta-ferrite content may be deliberately limited to a maximum of 30%, since at higher delta ferrite levels toughness could decrease again.
  • the austenitic portion of 70% -95% has high carbon solubility, effectively counteracting the formation of chromium carbides and the associated relatively high susceptibility to intergranular corrosion.
  • a delta ferrite content between 10% and 15% can be provided, corresponding to an austenite content between 90% and 85%.
  • a mainly martensitic microstructure with a small proportion of delta ferrite in the extent of 5% -30% (preferably 10% -15%) can be present in the core area of the blank.
  • the delta-ferrite content may be deliberately limited to a maximum of 30%, since at higher delta ferrite levels toughness could decrease again.
  • a mainly martensitic structure may be present in the edge zone of the blank, so that a high degree of hardening can be achieved.
  • the step of case-hardening the blank with nitrogen from the gas phase preferably at temperatures between 1000 ° C. and 150 ° C., particularly preferably between 1030 ° C. and 1100 ° C., and / or a nitrogen partial pressure between 0.05 bar and 0.3 bar, more preferably between 0.10 bar and 0.20 bar, provided, preferably following the step of processing the blank.
  • the edge zone of the blank can be selectively modified in a particularly advantageous manner for screw application.
  • nitrogen can be dissolved in the edge zone of the austenitic basic structure.
  • such surface hardening could have a surface hardness of 580 HV0.3 or higher with an ultimate hardness of 550 HV0.3 at a distance from the surface of 0.15-0.30 mm (which would be particularly advantageous for concrete screws can) or 0.1 - 0.15 mm (which can be particularly advantageous for self-tapping screws) can be achieved.
  • This in turn can provide good resistance to thread wear, even when grouting in concrete as well Reinforcing iron guarantee, which in turn allows a high load capacity of the screw.
  • the dissolved nitrogen can increase the PRE index in the edge zone locally to 23 or higher and thereby significantly improve the resistance to pitting corrosion, preferably to a level comparable to a 1.4401 steel.
  • the electrochemical parameter of the "breakthrough potential" can also be brought to a level comparable to a 1.4401 steel
  • the upper limit of the nitrogen partial pressure of 0.3 bar or 0.20 bar has the background that hereby forms the formation of chromium-containing and / or nitrogen-containing precipitates
  • the lower limit of the nitrogen partial pressure of 0.05 bar or 0.10 bar has the background that only after this pressure a significant effect of the nitrogen occurs.
  • the atmosphere provided in the step of case hardening can be purer In particular, a pure nitrogen atmosphere may be provided, provided that the process is carried out in a low pressure furnace a dilution, for example, with noble gases.
  • the case hardening of the blank with nitrogen from the gas phase in combination with a carburizing of the blank with carbon from the gas phase in addition to an increase in the nitrogen content, it is additionally possible to provide an increase in the carbon content as a result of carbon dioxide being diffused from the gas phase.
  • This embodiment is based on the finding that with simultaneous availability of carbon and nitrogen, the solubility of both elements can be increased simultaneously, with a higher nitrogen content while avoiding carbides and nitrides, a further advantageous increase in hardness and corrosion resistance can be achieved.
  • gaseous nitrogenous and carbonaceous media may be introduced into the process chamber separately and alternately.
  • a gas mixture that provides both carbon and nitrogen can be used (for example, ethyne, C2H2, along with N2).
  • the method may comprise the step of "processing the blank.”
  • the blank may be shaped into the shape of the shaped body, for example, the machining may include forming a thread on the blank on Cold forming, preferably rolling, of the blank.
  • the step of insert hardening of the blank takes place subsequent to the step of processing the blank. Accordingly, the blank is processed before curing.
  • the temporal reordering of the case hardening to the editing can simplify the processing and ensure particularly homogeneous product properties.
  • the step of case-hardening may suitably be a step of deep-freezing the blank, preferably at temperatures below minus 80 ° C., more preferably at a temperature of minus 150 ° C., and then tempering the blank, preferably at temperatures between 150 ° C. and 500 ° C, more preferably at temperatures between 200 ° C and 250 ° C, and / or and hold times between 1 hour and 5 hours, follow.
  • a step of deep-freezing the blank preferably at temperatures below minus 80 ° C., more preferably at a temperature of minus 150 ° C.
  • tempering the blank preferably at temperatures between 150 ° C. and 500 ° C, more preferably at temperatures between 200 ° C and 250 ° C, and / or and hold times between 1 hour and 5 hours, follow.
  • the blank is conveniently in the form of wire at the beginning of the process, ie it is a wire-shaped semi-finished product, which can further reduce the expense.
  • the invention is particularly suitable for the production of screws. It is therefore particularly preferred that the shaped body is a helical shape, preferably with a screw shank and a thread arranged on the screw shank.
  • the helical shape can form part of a finished screw or preferably the entire screw at the end of the process, that is to say preferably a monolithic screw is provided.
  • a local induction hardening of a tip region of the helical shape and, preferably, thereafter a deep cooling of the helical shape can be provided.
  • Inductive hardening at the screw tip can provide a localized increase in hardness to 580-700 HV0.3 without compromising toughness in failure critical areas of the screw, such as in the head, under head and / or shaft area.
  • the invention also relates to the aforementioned steel as such, namely a steel with 0.07 to 0.14 wt .-% carbon, preferably 0.08 to 0.12 wt .-% carbon, 13 to 15 wt .-% chromium, 1, 3 to 1, 7 wt .-% molybdenum, 1, 5 to 2.0 wt .-% nickel and 1, 0 to 1, 5 wt .-%, preferably 1, 2 wt .-%, manganese.
  • the invention also relates to the use of a steel according to the invention for producing a screw and / or a screw, which at least partially has a steel according to the invention and / or which is obtainable in a process according to the invention, in particular.
  • the screw may preferably be a self-tapping screw. It can for example be a concrete screw, that is a screw for cutting in concrete, or even a self-drilling screw for sheets.
  • the screw is a monolithic screw.
  • the ratio of the outside diameter of a thread of the screw to the thread pitch of the thread may be in the range of 1 to 2, in particular in the range of 1, 2 to 1, 45. These are typical thread dimensions for screws intended for self-tapping screwing into mineral substrates such as concrete. Under the slope can be understood in particular the axial distance of successive turns of a thread.
  • a concrete substrate may be provided with a bore into which a screw according to the invention is screwed, wherein in the concrete substrate a negative mold to the cutting thread of the screw is formed. Accordingly, the screw is self-tapping screwed into the bore in the concrete substrate to form a counter-thread.
  • the steel according to the invention contains 0.08 to 0.12 wt .-% carbon, which can be even more advantageous material properties, especially with regard to screw applications achieve.
  • Figure 1 a schematic flow diagram of an inventive
  • FIG. 1 schematically shows the sequence of steps of a possible embodiment of a production method according to the invention.
  • step 1 a blank, preferably wire-shaped, of a steel containing 0.07 to 0.14% by weight, preferably 0.08 to 0.12% by weight of carbon, 13 to 15% by weight of chromium, 1, 3 to 1, 7 wt .-% molybdenum, 1, 5 to 2.0 wt .-% nickel and 1, 0 to 1, 5 wt .-% manganese provided.
  • the steel may have other admixtures customary in the steel, for example vanadium (in particular ⁇ 0.2% by weight), niobium (in particular ⁇ 0.2% by weight), titanium (in particular ⁇ 0.2% by weight) and / or silicon (in particular ⁇ 0.5% by weight).
  • the remainder is iron with unavoidable impurities, for example sulfur and / or phosphorus, in particular in each case ⁇ 0.02% by weight.
  • the blank is processed in step 2, for example, formed, preferably rolled, and the blank thereby brought into the shape of a shaped body, in particular in the form of a helical shape with a screw shaft 20 and a screw shaft 20 arranged on the thread 21.
  • the screw shape may also have a rotary drive 15, for example a screw head, arranged on the screw shank 20.
  • the step 2 of machining may include, in addition to rolling, upsetting of the blank.
  • the formed as a helical shape blank is then cured in step 3 at a temperature greater than 900 ° C, in particular between 1000 ° C and 1 150 ° C, more preferably between 1030 ° C and 1 100 ° C, in a nitrogen-containing gas atmosphere, wherein the nitrogen partial pressure the gas atmosphere is preferably between 0.05 bar and 0.6 bar, preferably less than 0.3 bar, and more preferably less than 0.20 bar.
  • the gas atmosphere may also contain carbon.
  • step 4 the blank designed as a helical shape is quenched in step 4, in particular gas-quenched.
  • step 5 follows a deep-freeze treatment of the form of a helical blank at temperatures below minus 80 °, for example at minus 150 ° C.
  • step 6 the blank formed as a helical shape is annealed in step 6, preferably in a temperature range between 150 ° C and 500 ° C, more preferably between 200 ° C and 250 ° C, and / or a holding time between 1 hour and 5 hours.
  • a local, preferably inductive, hardening can be provided at a tip region of the blank designed as a helical shape, and preferably a subsequent deep-freezing of the blank formed as a helical shape.
  • the screw 10 has a cylindrical screw shaft 20, at the end of a hexagonal screw head is provided, which forms a rotary drive 15.
  • a thread 21 designed as a cutting thread extends with an outer diameter d and a pitch p.
  • a smaller-diameter support thread 28 may be provided on the screw shaft 20.
  • the screw shank 20 of the screw is screwed into a bore in a mineral substrate 50, in particular in a concrete substrate, wherein the thread 21 formed as a cutting thread has cut free a corresponding thread in the substrate 50 during screwing.
  • the screw shaft 20 is guided through a hole in an attachment 53 which is secured to the substrate 50 by the rotary drive 15 designed as a screw head.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Articles (AREA)
  • Forging (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Abstract

L'invention concerne un acier comprenant de 0,07 à 0,14 % en poids de carbone, de 13 à 15 % en poids de chrome, de 1,3 à 1,7 % en poids de molybdène, de 1,5 à 2,0 % en poids de nickel et de 1,0 à 1,5 % en poids de manganèse, ainsi que son utilisation pour fabriquer des vis.
EP18735215.8A 2017-06-26 2018-06-20 Acier durcissable par formation de martensite et son utilisation, en particulier destiné à fabriquer une vis Active EP3645756B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP17177789.9A EP3421623A1 (fr) 2017-06-26 2017-06-26 Acier durcissable par formation de martensite et son utilisation, en particulier destiné à fabriquer une vis
PCT/EP2018/066405 WO2019002044A1 (fr) 2017-06-26 2018-06-20 Acier à trempe martensitique et son utilisation, en particulier pour fabriquer une vis

Publications (2)

Publication Number Publication Date
EP3645756A1 true EP3645756A1 (fr) 2020-05-06
EP3645756B1 EP3645756B1 (fr) 2021-04-21

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EP17177789.9A Withdrawn EP3421623A1 (fr) 2017-06-26 2017-06-26 Acier durcissable par formation de martensite et son utilisation, en particulier destiné à fabriquer une vis
EP18735215.8A Active EP3645756B1 (fr) 2017-06-26 2018-06-20 Acier durcissable par formation de martensite et son utilisation, en particulier destiné à fabriquer une vis

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EP17177789.9A Withdrawn EP3421623A1 (fr) 2017-06-26 2017-06-26 Acier durcissable par formation de martensite et son utilisation, en particulier destiné à fabriquer une vis

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US (1) US20200063231A1 (fr)
EP (2) EP3421623A1 (fr)
JP (1) JP2020519757A (fr)
CN (1) CN110582585A (fr)
AU (1) AU2018293056A1 (fr)
BR (1) BR112019022958A2 (fr)
CA (1) CA3061570A1 (fr)
RU (1) RU2020102854A (fr)
TW (1) TW201905340A (fr)
WO (1) WO2019002044A1 (fr)

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* Cited by examiner, † Cited by third party
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EP3536812A1 (fr) * 2018-03-08 2019-09-11 HILTI Aktiengesellschaft Vis composée de deux métaux à acier marténsitique thermodurcissable
DE102018212111A1 (de) * 2018-07-20 2020-01-23 Robert Bosch Gmbh Verfahren zur Herstellung eines Bauteils aus einem Stahl mit einer stickstoffhaltigen Schutzschicht und entsprechend hergestelltes Bauteil
EP3869051A1 (fr) 2020-02-18 2021-08-25 Hilti Aktiengesellschaft Vis inoxydable bimétallique
EP3916245A1 (fr) 2020-05-28 2021-12-01 Hilti Aktiengesellschaft Vis avec filet hélicoïdal séparé et départ de filetage intégré
EP3916246A1 (fr) 2020-05-28 2021-12-01 Hilti Aktiengesellschaft Filet hélicoïdal de vis séparé fixé au moyen de griffes
DE102021006491B3 (de) 2021-12-30 2023-06-07 Hsiang Wu Verfahren zur herstellung eines befestigungselements aus rostfreiem stahl

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US5002729A (en) * 1989-08-04 1991-03-26 Carpenter Technology Corporation Case hardenable corrosion resistant steel alloy and article made therefrom
DE4033706A1 (de) 1990-10-24 1991-02-21 Hans Prof Dr Ing Berns Einsatzhaerten mit stickstoff zur verbesserung des korrosionswiderstandes martensitischer nichtrostender staehle
JP3340225B2 (ja) * 1993-01-12 2002-11-05 新日本製鐵株式会社 耐銹性に優れた高強度マルテンサイト系ステンレス鋼およびドリリングタッピンねじ
DE19626833A1 (de) 1996-07-04 1998-01-08 Hans Prof Dr Ing Berns Verfahren zur Erzeugung einer hochkorrosionsbeständigen martensitischen Randschicht über einem ferritisch-martensitischen Kern in Bauteilen aus nichtrostendem Stahl
JPH1036945A (ja) * 1996-07-19 1998-02-10 Nippon Steel Corp ねじ込み性に優れた高耐銹性マルテンサイト系ステンレス製ドリリングタッピンねじ及びその焼入方法
JP4252145B2 (ja) * 1999-02-18 2009-04-08 新日鐵住金ステンレス株式会社 耐遅れ破壊性に優れた高強度・高靭性ステンレス鋼
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JP6247477B2 (ja) * 2012-08-31 2017-12-13 日東精工株式会社 高周波焼入タッピンねじ
DE102012216117A1 (de) 2012-09-12 2014-03-13 Hilti Aktiengesellschaft Verfahren zum Herstellen einer selbstschneidenden Schraube
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JP2020519757A (ja) 2020-07-02
US20200063231A1 (en) 2020-02-27
AU2018293056A1 (en) 2019-11-21
BR112019022958A2 (pt) 2020-05-19
TW201905340A (zh) 2019-02-01
RU2020102854A3 (fr) 2021-09-14
RU2020102854A (ru) 2021-07-27
WO2019002044A1 (fr) 2019-01-03
EP3645756B1 (fr) 2021-04-21
EP3421623A1 (fr) 2019-01-02
CN110582585A (zh) 2019-12-17
CA3061570A1 (fr) 2019-10-25

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